Elastic blends of semicrystalline propylene polymers and high glass transition temperature materials

ABSTRACT

Compositions are provided having from 70 wt % to 95 wt % of a polymer selected from homopolymers and random copolymers of propylene and from 5 wt % to 30 wt % of a miscible hydrocarbon resin with a glass transition temperature greater than 20° C. The polymer has a heat of fusion of less than 50 J/g, a melt index (MI) of less than 20 dg/min, and contains stereoregular propylene crystallinity. Also provided are films containing such compositions, and articles, such as diapers or incontinence garments, including such films.

FIELD OF THE INVENTION

[0001] The present invention relates to elastic blends ofsemicrystalline, propylene-containing polymers and low molecular weight,high glass transition temperature materials which are miscible with thesemicrystalline propylene-containing polymers.

BACKGROUND

[0002] U.S. Patent Application Publication No. 2002/0019507 disclosesadhesive blends that can include a semi-crystalline copolymer ofpropylene and at least one comonomer selected from ethylene and at leastone C₄ to C₂₀ alpha-olefin, wherein the copolymer has a weight averagemolecular weight (M_(w)) from about 15,000 to about 200,000, a meltindex (MI) from about 7 dg/min to about 3000 dg/min, and a M_(w)/M_(n)of approximately 2. Also described are adhesive compositions havingpolymers or polymer blends with melt flow rates (MFRs) equal to andabove 250 dg/min at 230° C.

[0003] Embodiments of the present invention may have one or moreadvantages over previously known materials, such as having an improvedbalance of elasticity, hysteresis properties, tensile modulus, andconstant tensile modulus over a range of extensions.

SUMMARY OF THE INVENTION

[0004] In one embodiment, the present invention provides a compositionincluding a polymer and a miscible hydrocarbon resin, the misciblehydrocarbon resin having a glass transition temperature greater than 20°C. The polymer is selected from the group consisting of homopolymers andrandom copolymers of propylene and has a heat of fusion as determined byDifferential Scanning Calorimetry (DSC) of less than 50 J/g, a meltindex (MI) of less than 5 dg/min., and contains stereoregular propylenecrystallinity.

[0005] In another embodiment, the present invention provides acomposition including from 70% to 95% by weight, based on the totalweight of the composition, of a polymer and from 5% to 30% by weight,based on the total weight of the composition, of a miscible hydrocarbonresin having a glass transition temperature greater than 20° C. Thepolymer is selected from the group consisting of homopolymers and randomcopolymers of propylene and has a heat of fusion as determined by DSC ofless than 50 J/g, a melt index (MI) of less than 20 dg/min, and containsstereoregular propylene crystallinity.

[0006] In a particular aspect of any of the embodiments describedherein, the composition has one or more of the followingcharacteristics, in any combination:

[0007] the composition has a tension set of less than 20%, or less than12%, or less than 10%;

[0008] the composition has a tension set TS and a 500% modulus M₅₀₀%conforming to the relationship: TS≦0.01*M₅₀₀%+12.5, where M is in unitsof psi;

[0009] the composition has a single glass transition temperature atleast 1° C. lower than the glass transition temperature of thehydrocarbon resin;

[0010] the composition has a tensile modulus at least 10% lower than thetensile modulus of the polymer;

[0011] the polymer is present in the composition in an amount within therange having a lower limit of 70%, 75%, or 80% by weight to an upperlimit of 90%, 95%, or 99% by weight, based on the total weight of thecomposition;

[0012] the polymer has isotactic stereoregular propylene crystallinity;

[0013] the polymer is a random copolymer of propylene and at least onecomonomer selected from ethylene, C₄-C₁₂ α-olefins, and combinationsthereof;

[0014] the polymer comprises from 2 wt % to 25 wt % polymerized ethyleneunits, based on the total weight of the polymer;

[0015] the polymer has a narrow compositional distribution;

[0016] the polymer has a melting point as determined by DSC of from 25°C. to 110° C., or from 35° C. to 70° C.;

[0017] the polymer has a heat of fusion as determined by DSC within therange having an upper limit of 50 J/g or 10 J/g and a lower limit of 1J/g or 3 J/g;

[0018] the polymer has a molecular weight distribution Mw/Mn of from 2.0to 4.5;

[0019] the polymer has a melt index (MI) of less than 7 dg/min, or lessthan 2 dg/min;

[0020] the hydrocarbon resin is present in the composition in an amountwithin the range having a lower limit of 1%, 5%, or 10% by weight to anupper limit of 15%, 18%, 20%, 25%, or 30% by weight, based on the totalweight of the composition;

[0021] the hydrocarbon resin is a hydrogenated cycloaliphatic resin;

[0022] the hydrocarbon resin has a molecular weight (Mn) of from 200 to5000, or from 200 to 1000, or from 500 to 1000; and

[0023] the hydrocarbon resin has a softening point within the rangehaving an upper limit of 180° C., or 150° C., or 140° C. and a lowerlimit of 80° C., or 120° C., or 125° C.

[0024] In another embodiment, the present invention provides an elasticfilm including at least one layer comprising any of the inventivecompositions described herein. In a particular aspect of thisembodiment, the film is a monolayer film. In another particular aspectof this embodiment, the film is a multilayer film.

[0025] In another embodiment, the invention provides a garmentstructure, such as diapers and incontinence garments, which include anyof the inventive compositions described herein.

BRIEF DESCRIPTION OF THE DRAWINGS

[0026]FIG. 1 is a graph of the lost energy versus 500% tensile modulusof several comparative and inventive films.

[0027]FIGS. 2 and 4 are graphs of the tension set versus 500% tensilemodulus of several comparative and inventive films.

[0028]FIGS. 3 and 5 are graphs of 500% tensile modulus/100% tensilemodulus wt % of additive of several comparative and inventive films.

DETAILED DESCRIPTION

[0029] Polymer

[0030] The polymer of the present invention is an elastic polymer with amoderate level of crystallinity due to stereoregular propylenesequences. The polymer can be: (A) a propylene homopolymer in which thestereoregularity is disrupted in some manner such as byregio-inversions; (B) a random propylene copolymer in which thepropylene stereoregularity is disrupted at least in part by comonomers;or (C) a combination of (A) and (B).

[0031] In one embodiment, the polymer further includes a non-conjugateddiene monomer to aid in vulcanization and other chemical modification ofthe blend composition. The amount of diene present in the polymer ispreferably less than 10% by weight, and more preferably less than 5% byweight. The diene may be any non-conjugated diene which is commonly usedfor the vulcanization of ethylene propylene rubbers including, but notlimited to, ethylidene norbornene, vinyl norbornene, anddicyclopentadiene.

[0032] In one embodiment, the polymer is a random copolymer of propyleneand at least one comonomer selected from ethylene, C₄-C₁₂ α-olefins, andcombinations thereof. In a particular aspect of this embodiment, thecopolymer includes ethylene-derived units in an amount ranging from alower limit of 2%, 5%, 6%, 8%, or 10% by weight to an upper limit of20%, 25%, or 28% by weight. This embodiment will also includepropylene-derived units present in the copolymer in an amount rangingfrom a lower limit of 72%, 75%, or 80% by weight to an upper limit of98%, 95%, 94%, 92%, or 90% by weight. These percentages by weight arebased on the total weight of the propylene and ethylene-derived units;i.e., based on the sum of weight percent propylene-derived units andweight percent ethylene-derived units being 100%. The ethylenecomposition of a polymer can be measured as follows. A thin homogeneousfilm is pressed at a temperature of about 150° C. or greater, thenmounted on a Perkin Elmer PE 1760 infrared spectrophotometer. A fullspectrum of the sample from 600 cm⁻¹ to 4000 cm⁻¹ is recorded and themonomer weight percent of ethylene can be calculated according to thefollowing equation: Ethylene wt %=82.585−111.987X+30.045X², wherein X isthe ratio of the peak height at 1155 cm⁻¹ and peak height at either 722cm⁻¹ or 732 cm⁻, whichever is higher. The concentrations of othermonomers in the polymer can also be measured using this method.

[0033] Comonomer content of discrete molecular weight ranges can bemeasured by Fourier Transform Infrared Spectroscopy (FTIR) inconjunction with samples collected by GPC. One such method is describedin Wheeler and Willis, Applied Spectroscopy, 1993, vol. 47, pp.1128-1130. Different but similar methods are equally functional for thispurpose and well known to those skilled in the art.

[0034] Comonomer content and sequence distribution of the polymers canbe measured by ¹³C nuclear magnetic resonance (¹³C NMR), and such methodis well known to those skilled in the art.

[0035] In one embodiment, the polymer is a random propylene copolymerhaving a narrow compositional distribution. In another embodiment, thepolymer is a random propylene copolymer having a narrow compositionaldistribution and a melting point as determined by DSC of from 25° C. to110° C. The copolymer is described as random because for a polymercomprising propylene, comonomer, and optionally diene, the number anddistribution of comonomer residues is consistent with the randomstatistical polymerization of the monomers. In stereoblock structures,the number of block monomer residues of any one kind adjacent to oneanother is greater than predicted from a statistical distribution inrandom copolymers with a similar composition. Historicalethylene-propylene copolymers with stereoblock structure have adistribution of ethylene residues consistent with these blockystructures rather than a random statistical distribution of the monomerresidues in the polymer. The intramolecular composition distribution(i.e., randomness) of the copolymer may be determined by ¹³C NMR, whichlocates the comonomer residues in relation to the neighbouring propyleneresidues. The intermolecular composition distribution of the copolymeris determined by thermal fractionation in a solvent. A typical solventis a saturated hydrocarbon such as hexane or heptane. The thermalfractionation procedure is described below. Typically, approximately 75%by weight, preferably 85% by weight, of the copolymer is isolated as oneor two adjacent, soluble fractions with the balance of the copolymer inimmediately preceding or succeeding fractions. Each of these fractionshas a composition (wt % comonomer such as ethylene or other α-olefin)with a difference of no greater than 20% (relative), preferably 10%(relative), of the average weight % comonomer of the copolymer. Thecopolymer has a narrow compositional distribution if it meets thefractionation test described above. To produce a copolymer having thedesired randomness and narrow composition, it is beneficial if (1) asingle sited metallocene catalyst is used which allows only a singlestatistical mode of addition of the first and second monomer sequencesand (2) the copolymer is well-mixed in a continuous flow stirred tankpolymerization reactor which allows only a single polymerizationenvironment for substantially all of the polymer chains of thecopolymer.

[0036] The crystallinity of the polymers may be expressed in terms ofheat of fusion. Embodiments of the present invention include polymershaving a heat of fusion, as determined by DSC, ranging from a lowerlimit of 1.0 J/g, or 3.0 J/g, to an upper limit of 50 J/g, or 10 J/g.Without wishing to be bound by theory, it is believed that the polymersof embodiments of the present invention have generally isotacticcrystallizable propylene sequences, and the above heats of fusion arebelieved to be due to the melting of these crystalline segments.

[0037] The crystallinity of the polymer may also be expressed in termsof crystallinity percent. The thermal energy for the highest order ofpolypropylene is estimated at 189 J/g. That is, 100% crystallinity isequal to 189 J/g. Therefore, according to the aforementioned heats offusion, the polymer has a polypropylene crystallinity within the rangehaving an upper limit of 65%, 40%, 30%, 25%, or 20%, and a lower limitof 1%, 3%, 5%, 7%, or 8%.

[0038] The level of crystallinity is also reflected in the meltingpoint. The term “melting point,” as used herein, is the highest peakamong principal and secondary melting peaks as determined by DSC,discussed above. In one embodiment of the present invention, the polymerhas a single melting point. Typically, a sample of propylene copolymerwill show secondary melting peaks adjacent to the principal peak, whichare considered together as a single melting point. The highest of thesepeaks is considered the melting point. The polymer preferably has amelting point by DSC ranging from an upper limit of 110° C., 105° C.,90° C., 80° C., or 70° C., to a lower limit of 0° C., 20° C., 25° C.,30° C., 35° C., 40° C., or 45° C.

[0039] The polymers used in the invention have a weight averagemolecular weight (Mw) within the range having an upper limit of5,000,000 g/mol, 1,000,000 g/mol, or 500,000 g/mol, and a lower limit of10,000 g/mol, 20,000 g/mol, or 80,000 g/mol, and a molecular weightdistribution Mw/Mn (MWD), sometimes referred to as a “polydispersityindex” (PDI), ranging from a lower limit of 1.5, 1.8, or 2.0 to an upperlimit of 40, 20, 10, 5, or 4.5. The Mw and MWD, as used herein, can bedetermined by a variety of methods, including those in U.S. Pat No.4,540,753 to Cozewith, et al., and references cited therein, or thosemethods found in Verstrate et al., Macromolecules, v. 21, p. 3360(1988), the descriptions of which are incorporated by reference hereinfor purposes of U.S. practices.

[0040] In one embodiment, the polymer has a Mooney viscosity, ML(1+4) @125° C., of 100 or less, 75 or less, 60 or less, or 30 or less. Mooneyviscosity, as used herein, can be measured as ML(1+4) @ 125° C.according to ASTM D1646, unless otherwise specified.

[0041] The polymers used in embodiments of the present invention canhave a tacticity index (m/r) ranging from a lower limit of 4 or 6 to anupper limit of 8, 10, or 12. The tacticity index, expressed herein as“m/r”, is determined by ¹³C nuclear magnetic resonance (NMR). Thetacticity index m/r is calculated as defined in H. N. Cheng,Macromolecules, 17, 1950 (1984). The designation “m” or “r” describesthe stereochemistry of pairs of contiguous propylene groups, “m”referring to meso and “r” to racemic. An m/r ratio of 1.0 generallydescribes a syndiotactic polymer, and an m/r ratio of 2.0 an atacticmaterial. An isotactic material theoretically may have a ratioapproaching infinity, and many by-product atactic polymers havesufficient isotactic content to result in ratios of greater than 50.

[0042] In one embodiment, the polymer has isotactic stereoregularpropylene crystallinity. The term “stereoregular” as used herein meansthat the predominant number, i.e. greater than 80%, of the propyleneresidues in the polypropylene or in the polypropylene continuous phaseof a blend, such as impact copolymer exclusive of any other monomer suchas ethylene, has the same 1,2 insertion and the stereochemicalorientation of the pendant methyl groups is the same, either meso orracemic.

[0043] An ancillary procedure for the description of the tacticity ofthe propylene units of embodiments of the current invention is the useof triad tacticity. The triad tacticity of a polymer is the relativetacticity of a sequence of three adjacent propylene units, a chainconsisting of head to tail bonds, expressed as a binary combination of mand r sequences. It is usually expressed for copolymers of the presentinvention as the ratio of the number of units of the specified tacticityto all of the propylene triads in the copolymer.

[0044] The triad tacticity (mm fraction) of a propylene copolymer can bedetermined from a ¹³C NMR spectrum of the propylene copolymer and thefollowing formula:${{mm}\quad {Fraction}} = \frac{{PPP}({mm})}{{{PPP}({mm})} + {{PPP}({mr})} + {{PPP}({rr})}}$

[0045] where PPP(mm), PPP(mr) and PPP(rr) denote peak areas derived fromthe methyl groups of the second units in the following three propyleneunit chains consisting of head-to-tail bonds:

[0046] The 13C NMR spectrum of the propylene copolymer is measured asdescribed in U.S. Pat. No. 5,504,172. The spectrum relating to themethyl carbon region (19-23 parts per million (ppm)) can be divided intoa first region (21.2-21.9 ppm), a second region (20.3-21.0 ppm) and athird region (19.5-20.3 ppm). Each peak in the spectrum was assignedwith reference to an article in the journal Polymer, Volume 30 (1989),page 1350. In the first region, the methyl group of the second unit inthe three propylene unit chain represented by PPP (mm) resonates. In thesecond region, the methyl group of the second unit in the threepropylene unit chain represented by PPP (mr) resonates, and the methylgroup (PPE-methyl group) of a propylene unit whose adjacent units are apropylene unit and an ethylene unit resonates (in the vicinity of 20.7ppm). In the third region, the methyl group of the second unit in thethree propylene unit chain represented by PPP (rr) resonates, and themethyl group (EPE-methyl group) of a propylene unit whose adjacent unitsare ethylene units resonates (in the vicinity of 19.8 ppm).

[0047] The calculation of the triad tacticity is outlined in thetechniques shown in U.S. Pat. No. 5,504,172. Subtraction of the peakareas for the error in propylene insertions (both 2,1 and 1,3) from peakareas from the total peak areas of the second region and the thirdregion, the peak areas based on the 3 propylene units-chains (PPP(mr)and PPP(rr)) consisting of head-to-tail bonds can be obtained. Thus, thepeak areas of PPP(mm), PPP(mr) and PPP(rr) can be evaluated, and hencethe triad tacticity of the propylene unit chain consisting ofhead-to-tail bonds can be determined.

[0048] The polymers of embodiments of the present invention have a triadtacticity of three propylene units, as measured by ¹³C NMR, of 75% orgreater, 80% or greater, 82% or greater, 85% or greater, or 90% orgreater.

[0049] In embodiments of the present invention, the polymer has a meltindex (MI) of 20 dg/min or less, 7 dg/min or less, 5 dg/min or less, or2 dg/min or less, or less than 2 dg/min. The determination of the MI ofthe polymer is according to ASTM D1238 (190° C., 2.16 kg). In thisversion of the method a portion of the sample extruded during the testwas collected and weighed. This is commonly referred to as themodification 1 of the experimental procedure. The sample analysis isconducted at 190° C. with a 1 minute preheat on the sample to provide asteady temperature for the duration of the experiment.

[0050] Polymers of the present invention are present in the inventiveblend compositions in an amount ranging from a lower limit of 70%, 75%,or 80%, or 82%, or 85% by weight based on the total weight of thecomposition, to an upper limit of 99%, 95%, or 90% by weight based onthe total weight of the composition.

[0051] The polymer may be produced by any process that provides thedesired polymer properties, in heterogeneous polymerization on asupport, such as slurry or gas phase polymerization, or in homogeneousconditions in bulk polymerization in a medium comprising largely monomeror in solution with a solvent as diluent for the monomers. Forindustrial uses, continuous polymerization processes are preferred.Homogeneous polymers are often preferred in the invention. For thesepolymers, preferably the polymerization process is a single stage,steady state, polymerization conducted in a well-mixed continuous feedpolymerization reactor. The polymerization can be conducted in solution,although other polymerization procedures such as gas phase or slurrypolymerization, which fulfil the requirements of single stagepolymerization and continuous feed reactors, are contemplated.

[0052] The polymer may be made advantageously by the continuous solutionpolymerization process described in WO 02/34795, advantageously in asingle reactor and separated by liquid phase separation from the alkanesolvent.

[0053] Polymers of the present invention may be produced in the presenceof a chiral metallocene catalyst with an activator and optionalscavenger. The use of single site catalysts is preferred to enhance thehomogeneity of the polymer. As only a limited tacticity is needed manydifferent forms of single site catalyst may be used. Possible singlesite catalysts are metallocenes, such as those described in U.S. Pat.No. 5,026,798, which have a single cyclopentadienyl ring, advantageouslysubstituted and/or forming part of a polycyclic structure, and ahetero-atom, generally a nitrogen atom, but possibly also a phosphorusatom or phenoxy group connected to a group 4 transition metal,preferably titanium but possibly zirconium or hafnium. A further exampleis Me₅CpTiMe₃ activated with B(CF)₃ as used to produce elastomericpolypropylene with an Mn of up to 4 million. See Sassmannshausen,Bochmann, Rosch, Lilge, J.Organomet. Chem. (1997) 548, 23-28.

[0054] Other possible single site catalysts are metallocenes which arebis cyclopentadienyl derivatives having a group transition metal,preferably hafnium or zirconium. Such metallocenes may be unbridged asin U.S. Pat. No. 4,522,982 or U.S. Pat. No. 5,747,621. The metallocenemay be adapted for producing a polymer comprising predominantlypropylene derived units as in U.S. Pat. No. 5,969,070 which uses anunbridged bis(2-phenyl indenyl) zirconium dichloride to produce ahomogeneous polymer having a melting point of above 79° C. Thecyclopentadienyl rings may be substituted and/or part of polycyclicsystems as described in the above U.S. Patents.

[0055] Other possible metallocenes include those in which the twocyclopentadienyl groups are connected through a bridge, generally asingle atom bridge such as a silicon or carbon atom with a choice ofgroups to occupy the two remaining valencies. Such metallocenes aredescribed in U.S. Pat. No. 6,048,950 which disclosesbis(indenyl)bis(dimethylsilyl) zirconium dichloride and MAO; WO 98/27154which discloses a dimethylsilyl bridged bisindenyl hafnium dimethyltogether with a non-coordinating anion activator; EP1070087 whichdiscloses a bridged biscyclopentadienyl catalyst which has elements ofasymmetry between the two cyclopentadienyl ligands to give a polymerwith elastic properties; and the metallocenes described in U.S. Pat.Nos. 6,448,358 and 6,265,212.

[0056] The manner of activation of the single site catalyst can vary.Alumoxane and preferably methyl alumoxane can be used. Higher molecularweights can be obtained using non-or weakly coordinating anionactivators (NCA) derived and generated in any of the ways amplydescribed in published patent art such as EP277004, EP426637, and manyothers. Activation generally is believed to involve abstraction of ananionic group such as the methyl group to form a metallocene cation,although according to some literature zwitterions may be produced. TheNCA precursor can be an ion pair of a borate or aluminate in which theprecursor cation is eliminated upon activation in some manner, e.g.trityl or ammonium derivatives of tetrakis pentafluorophenyl boron (SeeEP277004). The NCA precursor can be a neutral compound such as a borane,which is formed into a cation by the abstraction of and incorporation ofthe anionic group abstracted from the metallocene (See EP426638).

[0057] In one embodiment, the polymer used in the present invention isdescribed in detail as the “Second Polymer Component (SPC)” in WO00/69963, WO 00/01766, WO 99/07788, WO 02/083753, and described infurther detail as the “Propylene Olefin Copolymer” in WO 00/01745, allof which are fully incorporated by reference herein for purposes of U.S.patent practice.

[0058] While the polymer by itself may have good elastic properties,addition of a miscible hydrocarbon resin can help to permit an easyextension over varying distances with a moderate and substantiallyconstant force of return from extension.

[0059] Hydrocarbon Resin

[0060] The resins of the present invention are selected to be misciblewith the polymer. The resins are miscible if they meet the followingcriteria. In a differential scanning calorimetry (DSC) experiment, apolymer composition including the polymer and other components such asprocess oil show a single glass transition temperature (Tg1) between 20°C. and −50° C.; a corresponding polymer blend containing the polymercomposition with the hydrocarbon resin added also show a single glasstransition temperature (Tg2); and Tg2 is higher than Tg1 by at least 1°C. The resins of the present invention preferably have a glasstransition temperature, by DSC, of greater than 20° C.

[0061] Resins used in embodiments of the present invention have asoftening point within the range having an upper limit of 180° C., 150°C., or 140° C., and a lower limit of 80° C., 120° C., or 125° C.Softening point (° C. ) is measured as a ring and ball softening pointaccording to ASTM E-28 (Revision 1996).

[0062] The resin is present in the inventive blend compositions in anamount ranging from a lower limit of 1%, 5%, or 10% by weight based onthe total weight of the composition, to an upper limit of 30%, or 25%,or 20%, or 18%, or 15% by weight based on the total weight of thecomposition.

[0063] Various types of natural and synthetic resins, alone or inadmixture with each other, can be used in preparing the compositionsdescribed herein, provided they meet the miscibility criteria describedherein. Suitable resins include, but are not limited to, natural rosinsand rosin esters, hydrogenated rosins and hydrogenated rosin esters,coumarone-indene resins, petroleum resins, polyterpene resins, andterpene-phenolic resins. Specific examples of suitable petroleum resinsinclude, but are not limited to aliphatic hydrocarbon resins,hydrogenated aliphatic hydrocarbon resins, mixed aliphatic and aromatichydrocarbon resins, hydrogenated mixed aliphatic and aromatichydrocarbon resins, cycloaliphatic hydrocarbon resins, hydrogenatedcycloaliphatic resins, mixed cycloaliphatic and aromatic hydrocarbonresins, hydrogenated mixed cycloaliphatic and aromatic hydrocarbonresins, aromatic hydrocarbon resins, substituted aromatic hydrocarbons,and hydrogenated aromatic hydrocarbon resins. As used herein,“hydrogenated” includes fully, substantially and at least partiallyhydrogenated resins. Suitable aromatic resins include aromatic modifiedaliphatic resins, aromatic modified cycloaliphatic resin, andhydrogenated aromatic hydrocarbon resins. Any of the above resins may begrafted with an unsaturated ester or anhydride to provide enhancedproperties to the resin. Examples of grafted resins and theirmanufacture are described in PCT Applications PCT/EP02/10794,PCT/EP02/10795, PCT/EP02/10796, and PCT/EP02/10686, which areincorporated herein by reference for U.S. purposes. For additionaldescription of resins, reference can be made to technical literature,e.g., Hydrocarbon Resins, Kirk-Othmer, Encyclopedia of ChemicalTechnology, 4th Ed. v.13, pp. 717-743 (J. Wiley & Sons, 1995).

[0064] Hydrogenated petroleum resins are usually prepared bycatalytically hydrogenating a thermally polymerized steam crackedpetroleum distillate fraction, especially a fraction having a boilingpoint of between 20° C. and 280° C. These fractions usually are ofcompounds having one or more unsaturated cyclic rings in the molecule,such as cyclodienes, cycloalkenes, and indenes. It is also possible tohydrogenate resins produced by the catalytic polymerization ofunsaturated hydrocarbons. Before hydrogenation occurs the polymerizedresin is usually dissolved in a saturated hydrocarbon solvent such asheptane. The hydrogenation catalysts that may be used include nickel,reduced nickel, or molybdenum sulphide. Hydrogenation can take place ina single stage at a temperature of 200° C. to 330° C., at a pressure of20.26 to 121.56 bar (20 to 120 atmospheres) for a period of 5 to 7hours. After filtering off the catalyst, the solvent is removed bydistillation and recovered for recycling. An improved hydrogenationprocess leading to increased yields of high quality hydrogenatedhydrocarbon resins is described in EP 0 082 726.

[0065] Resins suited for use as described herein include EMPR 100, 101,102, 103, 104, 105, 106, 107, 108, 109, 110, 116, 117, and 118 resins,OPPERA™ resins, and EMFR resins available from ExxonMobil ChemicalCompany, ARKON™ P140, P125, P115, M115, and M135 and SUPER ESTER™ rosinesters available from Arakawa Chemical Company of Japan, SYLVARES™polyterpene resins, styrenated terpene resins and terpene phenolicresins available from Arizona Chemical Company, SYLVATAC™ and SYLVALITE™rosin esters available from Arizona Chemical Company, NORSOLENE™aliphatic aromatic resins available from Cray Valley of France,DERTOPHENE™ terpene phenolic resins and DERCOLYTE™ polyterpene resinsavailable from DRT Chemical Company of France, EASTOTAC™ resins,PICCOTAC™ resins, REGALITE™ and REGALREZ™ hydrogenatedcycloaliphatic/aromatic resins available from Eastman Chemical Companyof Kingsport, Tenn., WINGTACK™ resins available from Goodyear ChemicalCompany, PICCOLYTE™ and PERMALYN™ polyterpene resins, rosins and rosinesters available from Hercules (now Eastman Chemical Company),coumerone/indene resins available from Neville Chemical Company,QUINTONE™ acid modified C₅ resins, C₅/C₉ resins, and acid modified C₅/C₉resins available from Nippon Zeon of Japan, CLEARON™ hydrogenatedterpene resins available from Yasuhara. The preceding examples areillustrative only and by no means limiting.

[0066] In one embodiment, the hydrocarbon resin has a number averagemolecular weight (Mn) within the range having an upper limit of 5000, or2000, or 1000, and a lower limit of 200, or 400, or 500, a weightaverage molecular weight (Mw) ranging from 500 to 5000, a Z averagemolecular weight (Mz) ranging from 500 to 10,000, and a polydispersity(PD) as measured by Mw/Mn of from 1.5 to 3.5, where Mn, Mw, and Mz aredetermined by size exclusion chromatography (SEC). In anotherembodiment, the hydrocarbon resin has a lower molecular weight than thepolymer.

[0067] Blend Composition

[0068] The compositions of the present invention include from a lowerlimit of 70%, 75%, or 80% by weight to an upper limit of 90%, 95%, or99% by weight of a polymer described above, based on the total weight ofthe composition, and from a lower limit of 1%, 5%, or 10% by weight toan upper limit of 15%, 18%, 20%, 25%, or 30% by weight of a misciblehydrocarbon resin as described above, based on the total weight of thecomposition.

[0069] Apart from the polymer component discussed above and thehydrocarbon resin, the composition may also include minor amounts ofother polymers, consistent with the physical properties desired. Suchadditive polymers include crystalline polypropylene including thosecommonly available as isotactic polypropylene, random copolymer andimpact copolymer. These polymers are differentiated from the polymersdescribed above in having a highest melting point of not less than 100°C. Also included within the scope of the invention is the addition ofvarious other polyolefin polymers such as low density and ultra lowdensity copolymers of ethylene and C₃-C₂₀ alpha olefins such aspropylene, butene, hexene and octene with a density in the range of 0.84to 0.96 g/cm³.

[0070] In one embodiment, the composition has a single glass transitiontemperature at 1° C. lower than the glass transition temperature of thehydrocarbon resin. In another embodiment, the composition has a singleglass transition temperature intermediate between the glass transitiontemperature of the hydrocarbon resin and the polymer described above. Inyet another embodiment, the composition has a glass transitiontemperature by DSC of 30° C. or lower, 20° C. or lower, 15° C. or lower,10° C. or lower, 7° C. or lower, 5° C. or lower, 3° C. or low or 1° C.or lower. The actual glass transition temperature of the blend dependson the composition (the relative amount of the hydrocarbon resins andthe polymer) and the glass transition temperature of the individualcomponents. This convergence of the glass transition of the blends fromthe values of the blend components is described by the Fox Floryrelationship.

[0071] As will be evident to those skilled in the art, the compositionsof the present invention can further include conventional additives toenhance a specific property, or such additives can be present as aresult of processing. Additives which may be incorporated include, forexample, fire retardants, antioxidants, plasticizers, and pigments.Other additives which may be used include, for example antiblockingagents, coloring agents, stabilizers, and oxidative-, thermal-, andultraviolet-light-inhibitors. Lubricants, mold release agents,nucleating agents, reinforcements, and fillers (including granular,fibrous, or powder-like) may also be used. Nucleating agents and fillerstend to improve the rigidity of the article. The list described hereinis not intended to be inclusive of all types of additives which may beused with the present invention. Those of skill in the art willappreciate that other additives may be used to enhance properties of thecomposition. As is understood by those skilled in the art, thecompositions of the present invention may be modified to adjust thecharacteristics of the blend as desired.

[0072] The compositions of the present invention can be prepared by anyprocedure that provides an intimate admixture of the various components.For example, the components can be combined by melt pressing thecomponents together on a Carver press to a thickness of about 0.5 mm(19.7 mls) and a temperature of about 180° C., rolling up the resultingslab, folding the ends together, and repeating the pressing, rolling,and folding operation about 10 times. Internal mixers are useful forsolution or melt blending. Also, blending at a temperature of about 180°C. to 240° C. in a Brabender Plastograph for about 1 to 20 minutes hasbeen found satisfactory. Still another method that can be used foradmixing the components involves blending the polymers in a Banburyinternal mixer above the flux temperature of all of the components, forexample, at 180° C. for about 5 minutes.

[0073] Batch-mixing procedures are typically supplanted by continuousmixing processes in the industry. These processes are well known in theart and include single and twin screw mixing extruders, static mixersfor mixing molten polymer streams of low viscosity, impingement mixers,as well as other machines and processes designed to disperse the polymerand resin in intimate contact.

[0074] Articles made from the blends of the invention include filmsobtained by casting or blowing and include those made by postfabrication orientation. Articles of the invention also include fibersand non-woven or woven fabrics made from these fibers. The blends of theinvention can also be used for the fabrication of articles by molding.These molding processes include but are not limited to rotomolding, blowmolding, slush molding as well as injection molding. The blends of theinvention are particularly suited for the fabrication of elastic filmsand molded articles by molding where the combination of low viscosityand excellent elastic properties are valuable.

[0075] Elongation and Tensile Strength

[0076] Elongation and tensile strength were measured as described below.The polymers of the current invention have an elongation of greater than1000%, or greater than 1200%, or greater than 1500%.

[0077] Tensile and elongation properties are determined at 20 in/min (51cm/min) according to the procedure described in ASTM D790. The data isreported in engineering units with no correction to the stress for thelateral contraction in the specimen due to tensile elongation. Thetensile and elongation properties of embodiments of our invention areevaluated using dumbbell-shaped samples. The samples are compressionmolded at 180° C. to 200° C. for 15 minutes at a force of 15 tons (133kN) into a plaque of dimensions 6 in×6 in (15 cm×15 cm). The cooledplaques are removed and the specimens are removed with a die and testedafter approximately 7 days. The elasticity evaluation of the samples isconducted on an Instron 4465, made by Instron Corporation of Canton,Mass. The digital data is collected in a file collected by the TestWorks program as commercially available from the Material TestingService of USA.

[0078] Elasticity

[0079] Embodiments of our invention are elastic after tensiledeformation. The elasticity, represented by the fractional increase inthe length of the sample, represented as a percentage of the length ofthe sample prior to deformation, is measured according to the generalprocedure ASTM D790. During tensile elongation, the polymer sample isstretched, and the polymer attempts to recover its original dimensionswhen the stretching force is removed. This recovery is not complete, andthe final length of the relaxed sample is slightly longer than that ofthe original sample. Elasticity is represented by the fractionalincrease in the length of the sample, expressed as a percentage of thelength of the original unstretched sample in that cycle of measurement.

[0080] The protocol for measuring the elasticity of the sample consistsof prestretching the deformable zone of the dumbbell, i.e., the narrowportion of the specimen, made according to the procedure described abovefor the measurement of elongation and tensile strength. The deformablezone of the dumbell is stretched by 200% of its original length toprestretch the sample. This prestretching is conducted at a deformationrate of 10 inches (25 cm) per minute. The work, expressed in in.lb. (orjoules) is reported as the Energy Loading. The sample is relaxed at thesame rate to form an analytical specimen which is a prestretchedspecimen of the original sample. The energy recovered during thecontraction of the sample is expressed as the Energy Unloading in unitsof in.lb (or joules). The Energy Unloading appears as a negative numberto describe energy derived from the sample. In the tables herein, thiscycle of deformation and contraction is referred to as Cycle 1. Thedifference between the Energy Loading and the absolute value of theEnergy Unloading is the Lost Energy. A useful comparative measure is theratio of the Lost energy to the Energy Loading, which is expressed asthe % Lost Energy. A second comparative measure is the distension in thelength of the polymer sample in the deformable zone at the point in thecycle where the retractive force is zero. The change in the length ofthe deformable zone expressed as a percentage of the original length isthe Tension Set. The purpose of this Cycle 1 cycle is not analytical butrather to precondition the sample for the actual analysis which is donein Cycle 2. The length of the sample after Cycle 1 is denoted d₁. InCycle 2, the sample is stretched by 200% of its length immediately afterCycle 1 is completed. This stretching is conducted at a deformation rateof 10 inches (25 cm) per minute. The sample is relaxed at the same rateuntil the contraction force on the sample is zero. The length of thesample when the contraction force on the sample is zero during Cycle 2is d2, and typically d2 is larger than d1. In Cycle 2 we show data inthe tables for energy loading, energy unloading, lost energy and % lostenergy which are measured the same way in this cycle as in Cycle 1. Thetension set of the sample in Cycle 2 expressed as a percent iscalculated as 100*(d₂−d₁)/d₁.

[0081] In one embodiment of the present invention, the compositionsdescribed herein have a tension set, as measured by the proceduredescribed above, of less than 50%, or less than 40%, or less than 30%,or less than 25%, or less than 20%, or less than 15%, or less than 12%,or less than 10%, or less than 7%, or less than 5%, or less than 3%.

[0082] In another embodiment, the composition can have a tension set TSand a 500% modulus M_(500%) conforming to the relationship:

[0083] TS≦0.01*M_(500%)+12.5,

[0084] where M is in units of psi.

[0085] The remarkable elasticity of the blends of the present inventionas shown by the low tension set values is also described by remarkablehysteresis properties. Hysteresis is used to describe a behaviour ofelastic materials where in a single or multiple cyclic deformationcomposed of a uniaxial deformation followed by unaxial contraction, asshown above for the determination of tension set, to essentially thesame original dimensions, the material does not display identicaldynamic properties in the distention and contraction parts of the cycle.Hysteresis properties are quantified using tension set, lost work, andcreep. For purposes of the present invention, acceptable hysteresisproperties are reflected by low values of all three of the descriptors.

[0086] Compositions of the present invention preferably havesimultaneously good elastic properties and low tensile modulus. Tensilemodulus is a measure of the extensional resistance of the elasticmaterial. A material with a high tensile modulus is hard to deform. Foruses such as elastic films and molded or extruded compositions, easyextension of the material is desired, and tensile modulus is thereforepreferably low. Low tensile modulus is especially preferred inapplications such as elastic materials in diapers, because at hightensile modulus values the retractive force may be large enough to causediscomfort to the wearer. In one embodiment, the composition has atensile modulus at least 10% lower than the tensile modulus of thepolymer. In another embodiment, the composition has a tensile modulus at500% elongation in the range having an upper limit of 1000 psi, or 800psi, or 600 psi, or 500 psi, or 400 psi, or 300 psi, or 200 psi and alower limit of 10 psi, or 20 psi, or 50 psi, or 75 psi, or 100 psi, or150 psi.

[0087] Compositions of the present invention preferably have anessentially invariant tensile modulus over a range of extensions,particularly within the range of 100% to 500% elongation. Constanttensile modulus over a range of extensions is especially desirable forelastic materials in diapers and similar applications, because the usersof diapers and other materials expect such materials to have a constantretractive force.

[0088] Film

[0089] One embodiment of the present invention provides a monolayer ormultilayer film including any of the inventive compositions describedherein.

[0090] The films of the present invention may be used in a variety ofapplications. For example, the films are suitable for diaperapplications and similar absorbent garments such as incontinencegarments.

[0091] One embodiment of the present invention includes a garmentstructure made from or including a film as described herein. In aparticular aspect of this embodiment, the garment structure is a diaperor an incontinence garment. Garments, such as diaper backsheets, can beformed by adhering the film to a garment substrate.

EXAMPLES

[0092] Mooney viscosity, as used herein, is measured as ML(1+4) @ 125°C. according to ASTM D1646.

[0093] Heat of fusion (ΔH_(fus) in the tables herein) and glasstransition temperature (Tg in the tables herein) were measured byDifferential Scanning Calorimetry (DSC) using the ASTM E-794-95procedure. The analyses were conducted on a Pyris 1 instrument using theaccompanying software available form Perkin Elmer Instruments, USA. Allmeasurements were conducted during the first heating cycle between −100°C. and +150° C. on a sample that had been molded at 200° C. and allowedto anneal at room temperature for approximately 7 days. The firstheating cycle was run at a temperature ramp rate of 20° C. /min. Theheat of fusion is measured from the total area under the peak curve inthe region of room temperature to 105° C. The glass transitiontemperature is the interpolated midpoint of the inflection point in theDSC trace corresponding to the largest change in the heat capacity ofthe sample.

[0094] Tensile and elongation properties are determined at 20 in/min (51cm/min) according to the procedure described in ASTM D790. The data isreported in engineering units with no correction to the stress for thelateral contraction in the specimen due to tensile elongation. Thetensile and elongation properties of embodiments of our invention areevaluated using dumbbell-shaped samples. The samples are compressionmolded at 180° C. to 200° C. for 15 minutes at a force of 15 tons (133kN) into a plaque of dimensions 6 in×6 in (15 cm×15 cm). The cooledplaques are removed and the specimens are removed with a die and testedafter approximately 7 days.

[0095] In the Examples below, Tensile Modulus at a particular elongationis abbreviated as M_(x%), where X is the elongation. Thus, M_(50%),M_(100%), M_(200%) and M_(500%) indicate the Tensile Modulus as 50%,100%, 200% and 500%, respectively. Tensile Modulus is reported in unitsof psi and MPa. The ratio of Tensile Modulus at 500% to Tensile Modulusat 100% is denoted M_(500%)/M₁₀₀%, and is dimensionless.

[0096] Tension set is measured according to the general procedure ASTMD790, and is conducted on an Instron 4465, made by Instron Corporationof Canton, Mass. The elasticity of the samples is expressed as a percentof the length of the original un-stretched sample.

[0097] Flexural modulus is measured in accordance with ASTM D790, usinga Type IV dogbone at crosshead speed of 0.05 in/min (1.3 mm/min).

[0098] MFR at 230° C. is determined according to the procedure of ASTMD1238 Procedure A (230° C., 2.16 kg).

[0099] The polymer components used in the following examples aredescribed in Table 1. TABLE 1 Mooney Viscosity 7 Day ΔH_(fus) POLYMERML(1 + 4)@125° C. wt % C₂ (J/g) Polymer-A 24 16.2 * Polymer-B 22 16.0 *Polymer-C 22 15.9 * Polymer-D 20.2 19.1 1.467 Polymer-E 24.8 16.8 4.5Polymer-F 24.4 16.8 3.589 Polymer-G 22 16.2 4.186 Polymer-H 21.9 15.310.382 Polymer-I 19.8 15.6 8.78 Polymer-J 18.2 14.8 13.728 Polymer-H 2416.4 * TOPAS Topas 8007 D62 from Targor PS Atactic polystyrene DowChemical Co, Midland, MI IPP Isotactic polypropylene ESC4292 fromExxonMobil Chemical Co., Houston, TX

[0100] Polymers A-H are ethylene-propylene random copolymer having theindicated weight percents of ethylene-derived units, and the balance ofpropylene-derived units, prepared using a metallocene catalyst system.

Example 1 Samples 1-7

[0101] Seven polymer blends were made by melt blending polymer-A withhydrocarbon resin EMPR 103 in the proportions indicated in Table 2, at175° C.-225° C. in a 250 cm³ Brabender internal mixer. The blends werethen fabricated into compression molded plaques and tested afterapproximately 7 days. Mechanical and hysteresis properties of the sevensamples were measured, and are reported in Tables 3 and 4, respectively.

[0102] Example 1 shows that the incorporation of hydrocarbon resins intopolymer-A leads to a lowering of the tensile modulus without significantchange in any of the other properties, such as tensile elongation andelastic recovery. TABLE 2 Composition Sample polymer-A EMPR 103 # (wt %)(wt %) 1 90 10 2 96 4 3 84 16 4 76 24 5 100 0 6 64 36 7 52 48

[0103] TABLE 3 Mechanical and Thermal Properties Sample M_(50%) M_(100%)M_(200%) M_(500%) M_(500%) Tg # (psi (MPa)) (psi (MPa)) (psi (MPa)) (psi(MPa)) M_(100%) (° C.) 1 185 216 243 436 2.02 −26.9 (1.28) (1.49) (1.68)(3.01) 2 207 247 284 540 2.18 −24.0 (1.43) (1.70) (1.96) 3.72) 3 159 186210 352 1.89 −20.6 (1.10) (1.28) (1.45) (2.43) 4 136 162 184 276 1.70−17.4 (0.938) (1.12) (1.27) 1.90) 5 277 312 337 613 1.96 −28.7 (1.91)(2.15) (2.32) (4.23) 6 137 162 187 257 1.58 −10.9 (0.945) (1.12) (1.29)1.77) 7 111 127 148 232 1.82 2.7 (0.765) (0.876) (1.02) 1.60)

[0104] TABLE 4 Hysteresis Properties Cycle 1 Cycle 2 Energy Energy LostLost Tension Energy Energy Lost Lost Tension Sample Loading UnloadingEnergy Energy Set Loading Unloading Energy Energy Set # (in. lb.(mJ))(in. lb. (mJ)) (in. lb. (mJ)) (%) (%) (in. lb. (mJ)) (in. lb. (mJ)) (in.lb. (mJ)) (%) (%) 1 18.9 −10.56 8.34 44.13 15.3 14.24 −11.18 3.06 21.57.3 (2140) (−1193)) (942) (1609) (−1263) (346) 2 17.73 −10.36 7.37 41.613.2 13.60 −11.05 2.55 18.8 6 (2003) (−1171) (833) (1537) (−1249) (288)3 13.36  −8.38 4.98 37.3 13.6 10.77  −8.76 2.01 18.7 6.4 (1510) (−947)(563) (1217) (−990) (227) 4 12.81  −7.64 5.17 40.4 14.1  9.95  −8.131.82 18.3 6.8 (1448) (−863)  ()584) (1120) (−919) (206) 5 19.97 −11.258.72 43.7 15.32 15.33 −11.88 3.45 22.50 7.34 (2257) (−1271) (985) (1732)(−1342) (390) 6 8.8  −5 3.8 43.2 18.6  7.3  −5.5 1.8 24.7 12.5 (990) (−560) (430) (820) (−620) (200) 7 6.5  −2.6 3.9 60.0 46.4  6.5  −3.3 3.249.2 47.6 (730)  (−290) (440) (730) (−370) (360)

Example 2 Samples 8-12

[0105] Polymer blends were made by melt blending polymer-A withisotactic polypropylene (“iPP”) in the proportions indicated in Table 5,at 175° C.-225° C. in a 250 cm³ Brabender internal mixer. The blendswere then fabricated into compression molded plaques and tested afterapproximately 7 days. Mechanical and hysteresis properties of the sevensamples were measured, and are reported in Tables 6 and 7, respectively.

[0106] Example 2 shows that the addition of iPP into polymer-A leads toincreased tensile modulus. TABLE 5 Composition Sample polymer-A iPP #(wt %) (wt %) 8 100 0 9 90 10 10 96 4 11 84 16 12 76 24

[0107] TABLE 6 Mechanical Properties Sample M_(50%) M_(100%) M_(200%)M_(500%) M_(500%) # (psi (MPa)) (psi (MPa)) (psi (MPa)) (psi (MPa))M_(100%) 8 277 312 337 613 1.96 (1.91) (2.15) (2.32) (4.23) 9 313 342396 803 2.35 (2.16) (2.36) (2.73) (5.54) 10 273 299 325 634 2.12 (1.88)(2.06) (2.24) (4.37) 11 345 378 461 914 2.42 (2.38) (2.61) (3.18) (6.30)12 534 624 811 1343 2.15 (3.68) (4.30) (5.59)  (9.260)

[0108] TABLE 7 Hysteresis Properties Cycle 1 Cycle 2 Energy Energy LostLost Tension Energy Energy Lost Lost Tension Sample Loading UnloadingEnergy Energy Set Loading Unloading Energy Energy Set # (in. lb.(mJ))(in. lb. (mJ)) (in. lb. (mJ)) (%) (%) (in. lb. (mJ)) (in. lb. (mJ)) (in.lb. (mJ)) (%) (%) 8 19.97 −11.25  8.72 43.7 15.32 15.33 −11.88  3.4522.5 7.341 (2257) (−1271) (985) (1732) (−1342) (390) 9 28.0 −12.5 15.555.4 18.2 19.0 −12.4 6.6 34.7 9.51 (3160) (−1410) (1750) (2150) (−1400)(750) 10 23.2 −11.7 11.5 49.6 17.7 16.8 −12.1 4.7 28.0 8.81 (2620)(−1320) (1300) (1900) (−1370) (530) 11 30.5 −13.4 17.1 56.1 19.1 21.4−13.9 7.5 35.0 10.91 (3450) (−1510) (1930) (2420) (−1570) (850) 12 50.4−15.4 35.0 69.4 28.5 34.2 −16.0 18.2  53.2 22.7 (5700) (−1740) (3960)(3860) (−1810)  (2060)

[0109]FIGS. 1, 2, and 3 illustrate the effect of adding EMPR 103 versusiPP to the polymer composition.

Example 3 Samples 13-16

[0110] Polymer blends were made by melt blending polymer-B withhydrocarbon resin EMPR 100A in the proportions indicated in Table 8, at175° C.-225° C. in a 250 cm³ Brabender internal mixer. The blends werethen fabricated into compression molded plaques and tested afterapproximately 7 days. Mechanical and hysteresis properties of the sevensamples were measured, and are reported in and 10, respectively. TABLE 8Composition Sample polymer-B EMPR 100A # (wt %) (wt %) 13 90 10 14 96 415 84 16 16 76 24

[0111] TABLE 9 Mechanical Properties Sample M_(50%) M_(100%) M_(200%)M_(500%) M_(500%) # (psi (MPa)) (psi (MPa)) (psi (MPa)) (psi (MPa))M_(100%) 13 158 179 186 253 1.41 (1.09) (1.23) (1.28) (1.74) 14 183 206214 289 1.41 (1.26) (1.42) (1.48) (1.99) 15  91 106 109 109 1.03 (0.63)(0.731) (0.752) (0.752) 16  77  93  99  92 0.99 (0.53) (0.64) (0.68)(0.63)

[0112] TABLE 10 Hysteresis Properties Cycle 1 Cycle 2 Energy Energy LostLost Tension Energy Energy Lost Lost Tension Sample Loading UnloadingEnergy Energy Set Loading Unloading Energy Energy Set # (in. lb.(mJ))(in. lb. (mJ)) (in. lb. (mJ)) (%) (%) (in. lb. (mJ)) (in. lb. (mJ)) (in.lb. (mJ)) (%) (%) 13 11.1 −7.6 3.5 31.5 16.1 10.0 −8.1 1.9 19.0 7.8(1250) (−860) (400) (1130) (−920) (210) 14 10.9 −5.2 5.7 52.3 18.5 10.5−8.5 2.0 19.0 9.2 (1230) (−590) (640) (1190) (−960) (230) 15  7.4 −4.03.4 45.9 26.3  6.4 −4.5 1.9 29.7 9.1 (840) (−450) (380) (720) (−510) 16 4.5 −2.6 1.9 42.2 36.6  4.1 −2.6 1.5 36.6 27.7 (510) (−290) (210) (460)(−290) (170)

[0113]FIGS. 4, 5, and 6 illustrate the effect of adding EMPR 100A versusiPP to the polymer composition.

Example 4 Examples 17-25

[0114] Polymer blends were made by melt blending polymer-A withhydrocarbon resin EMPR 103 and iPP in the proportions indicated in Table11, at 175° C.-225° C. in a 250 cm³ Brabender internal mixer. The blendswere then fabricated into compression molded plaques and tested afterapproximately 7 days. Mechanical and hysteresis properties of the sevensamples were measured, and ara reported in Tables 12 and 13,respectively. TABLE 11 Composition Sample polymer-A EMPR 103 iPP # (wt%) (wt %) (wt %) 17 80 4 16 18 72 4 24 19 88 4 8 20 84 10 6 21 78 10 1222 72 10 18 23 80 16 4 24 76 16 8 25 72 16 12

[0115] TABLE 12 Mechanical Properties Sample M_(50%) M_(100%) M_(200%)M_(500%) M_(500%) # (psi (MPa)) (psi (MPa)) (psi (MPa)) (psi (MPa))M_(100%) 17 328 371 468 947 2.55 (2.26) (2.56) (3.23) (6.53) 18 457 640735 1310 2.05 (3.15) (4.41) (5.07) (9.03) 19 275 298 354 729 2.45 (1.90)(2.05) (2.44) (5.03) 20 225 254 289 581 2.29 (1.55) (1.75) (1.99) (4.01)21 263 297 352 726 2.44 (1.81) (2.05) (2.43) (5.01) 22 291 333 428 9172.75 (2.01) (2.30) (2.95) (6.32) 23 190 218 246 463 2.12 (1.31) (1.50)(1.70) (3.19) 24 206 237 274 583 2.46 (1.42) (1.63) (1.89) (4.02) 25 227262 310 672 2.56 (1.57) (1.81) (2.14) (4.63)

[0116] TABLE 13 Hysteresis Properties Cycle 1 Cycle 2 Energy Energy LostLost Tension Energy Energy Lost Lost Tension Sample Loading UnloadingEnergy Energy Set Loading Unloading Energy Energy Set # (in. lb.(mJ))(in. lb. (mJ)) (in. lb. (mJ)) (%) (%) (in. lb. (mJ)) (in. lb. (mJ)) (in.lb. (mJ)) (%) (%) 17 27.35 −12.12 15.23 55.69 18.7 19.1 −12.6 6.5 34.0310.9 (3091) (−1370) (1721) (2160) (−1420) (730) 18 38.8 −13.1 25.7 66.2424.4 26.5 −13.7 12.8 48.30 18.5 (4380) (−1480) (2900) (3000) (−1550) (1450) 19 22.8 −11.5 11.3 49.56 17.2 16.5 −12.0 4.5 27.27 8.8 (2580)(−1300) (1280) (1860) (−1360) (510) 20 19.7 −10.4 9.3 47.21 16.3 14.4−10.9 3.5 24.30 7.6 (2230) (−1180) (1050) (1630) (−1230) (400) 21 22.3−11.0 11.3 50.67 16.9 15.9 −11.4 4.5 28.30 8.8 (2520) (−1240) (1280)(1800) (−1290) (510) 22 25.7 −11.2 14.5 56.42 17.7 17.3 −11.4 5.9 34.1011.8 (2900) (−1270) (1640) (1950) (−1290) (670) 23 16.4 −9.0 7.4 45.1216 12.3 −9.6 2.7 21.95 7.4 (1850) (−1000) (840)  (1390) (−1100) (300) 2418.3 −9.5 8.8 48.09 16.7 13.28 −10.0 3.28 24.69 8.5 (2070) (−1100)(990)  (1501) (−1130) (371) 25 20.2 −10.2 10.0 49.5 16.6 14.5 −10.8 3.725.51 16.6 (2280) (−1150) (1130) (1640) (−1220) (420)

Example 5 Examples 26-46

[0117] Polymer blends were made by melt blending various polymercompositions having different compositions and crystallinities withhydrocarbon resin EMPR 103 in the proportions indicated in Table 14, at175° C.-225° C. in a 250 cm³ bender internal mixer. The blends were thenfabricated into compression molded plaques and tested afterapproximately 7 days. Mechanical and hysteresis properties of the sevensamples were measured, and are reported in Tables 15 and 16,respectively. The “polymer type” indicated in Table 14 to thedesignations of Table 1. TABLE 14 Composition Polymer Sample Type AmountEMPR 103 # (Table 1) (wt %) (wt %) 26 D 88 12 27 D 84 16 28 D 80 20 29 E88 12 30 E 84 16 31 E 80 20 32 F 88 12 33 F 84 16 34 F 80 20 35 G 88 1236 G 84 16 37 G 80 20 38 H 88 12 39 H 84 16 40 H 80 20 41 I 88 12 42 I84 16 43 I 80 20 44 J 88 12 45 J 84 16 46 J 80 20

[0118] TABLE 15 Mechanical and Thermal Properties Tensile Sample M_(50%)M_(100%) M_(200%) M_(500%) Elongation Strength Tg # (psi (MPa)) (psi(MPa)) (psi (MPa)) (psi (MPa)) (%) (psi (MPa)) (° C.) 26  73  87  87  66137 89 −25.5 (0.50) (0.60) (0.60) (0.46) (0.61)  27  72  87  89  68 * 92−24.7 (0.50) (0.60) (0.61) (0.47) (0.63)  28  67  81  83  64 151 85−22.3 (0.46) (0.56) (0.57) (0.44) (0.59)  29 153 185 204 298 844 967−22. (1.05) (1.28) (1.41) (2.05) (6.67)  30 121 145 160 202 908 640−22.7 (0.834) (1.00) (1.10) (1.39) (4.41)  31 113 137 153 187 887 524−21.2 (0.779) (0.945) (1.05) (1.29) (3.61)  32 103 123 129 135 987 416−23.2 (0.710) (0.848) (0.889) (0.931) (2.87)  33  94 112 119 118 * 339−22.1 (0.65) (0.772) (0.821) (0.814) (2.34)  34  86 103 111 106 * 277−20.5 (0.59) (0.710) (0.765) (0.731) (1.91)  35 113 133 141 158 907 448−23.5 (0.779) (0.917) (0.972) (1.09) (3.09)  36 100 119 128 134 998 400−22.0 (0.690) (0.821) (0.883) (0.924) (2.76)  37  96 115 124 127 1000365 −20.1 (0.66) (0.793) (0.855) (0.876) (2.52)  38 189 224 247 395 8181201 −22.8 (1.30) (1.54) (1.70) (2.72) (8.281) 39 167 199 221 326 8481010 −21.0 (1.15) (1.37) (1.52) (2.25) (6.964) 40 144 174 196 276 870838 −19.7 (0.993) (1.20) (1.35) (1.90) (5.78)  41 175 207 228 336 8551039 −21.6 (1.21) (1.43) (1.57) (2.32) (7.164) 42 152 183 204 296 870895 −20.1 (1.05) (1.26) (1.41) (2.04) (6.17)  43 131 157 176 237 903 706−21.2 (0.903) (1.08) (1.21) (1.63) (4.87)  44 211 247 267 426 802 1245−20.1 (1.46) (1.70) (1.84) (2.94) (8.584) 45 191 226 248 382 831 1198−18.9 (1.32) (1.56) (1.71) (2.63) (8.260) 46 161 192 215 314 860 954−18.1 (1.11) (1.32) (1.48) (2.16) (6.58) 

[0119] TABLE 16 Hysteresis Properties Cycle 1 Cycle 2 Energy Energy LostEnergy Energy Lost Loading Unloading Energy Lost Tension LoadingUnloading Energy Lost Tension Sample (in. lb. (in. lb. (in. lb. EnergySet (in. lb. (in. lb. (in. lb. Energy Set # (mJ)) (mJ)) (mJ)) (%) (%)(mJ)) (mJ)) (mJ)) (%) (%) 26 4.7 −1.5 3.2 68.1 42.7 5.0 −2.7 2.3 46.036.2 (530) (−170) (360) (560) (−300) (260) 27 4.8 −1.8 3.0 62.5 41 4.9−2.8 2.1 42.9 33.4 (540) (−200) (340) (550) (−320) (240) 28 5.1 −2.4 2.752.9 40 4.6 −2.7 1.9 41.3 32.5 (580) (−270) (300) (520) (−300) (210) 2913.3 −8.6 4.7 35.3 15 11.0 −9.3 1.7 15.5 5.3 (1500)  (−970) (530)(1240)  (−1050)  (190) 30 11.3 −7.1 4.2 37.2 17.3 9.5 −7.6 1.9 20.0 8.5(1280)  (−800) (470) (930) (−860) (210) 31 9.6 −6.0 3.6 37.5 17.2 8.2−6.4 1.8 22.0 8.5 (1100)  (−680) (410) (930) (−720) (200) 32 9.1 −4.94.2 46.2 25 7.8 −5.6 2.2 28.2 17.2 (1000)  (−550) (470) (880) (−630)(250) 33 8.4 −4.7 3.7 44.0 24.4 7.0 −5.1 1.9 27.1 17.5 (950) (−530)(420) (790) (−580) (210) 34 7.5 −4.3 3.2 42.7 24.1 6.4 −5.5 0.9 14.118.1 (850) (−490) (360) (720) (−620) (100) 35 9.9 −5.5 4.4 44.4 22.6 8.2−6.0 2.2 26.8 16 (1100)  (−620) (500) (930) (−680) (250)

[0120] TABLE 16 Hysteresis Properties (continued) Cycle 1 Cycle 2 EnergyEnergy Lost Energy Energy Lost Loading Unloading Energy Lost TensionLoading Unloading Energy Lost Tension Sample (in. lb. (in. lb. (in. lb.Energy Set (in. lb. (in. lb. (in. lb. Energy Set # (mJ)) (mJ)) (mJ)) (%)(%) (mJ)) (mJ)) (mJ)) (%) (%) 36 8.6 −4.7 3.9 45.3 23.1 7.2 −5.3 1.926.4 16.7  (970) (−530) (440)  (810) (−600) (210) 37 8.6 −4.9 3.7 43.021.9 7.1 −5.3 1.8 25.4 15.2  (970) (−550) (420)  (800) (−600) (200) 3816.3 −10.2 6.1 37.4 13.3 12.7 −10.7 2.0 15.7 4.5 (1840) (−1150)  (690)(1430) (−1210)  (230) 39 14.2 −8.9 5.3 37.3 13.7 11.2 −9.4 1.8 16.1 5(1600) (−1000)  (600) (1270) (−1060)  (200) 40 12.3 −7.7 4.6 37.4 14.310.0 −8.3 1.7 17.0 5.9 (1390) (−870) (520) (1130) (−940) (190) 41 14.8−8.9 5.9 39.9 14.1 11.6 −9.7 1.9 16.4 5.6 (1670) (−1000)  (670) (1310)(−1100)  (210) 42 12.6 −7.8 4.8 38.1 14.3 9.9 −8.3 1.6 16.2 5.8 (1420)(−880) (540) (1100) (−940) (180) 43 11.0 −6.5 4.5 40.9 15.3 8.7 −7.0 1.719.5 7.1 (1240) (−730) (510)  (980) (−790) (190) 44 17.0 −9.8 7.2 42.414.4 12.8 −10.6 2.2 17.2 5.6 (1920) (−1110)  (810) (1450) (−1200)  (250)45 15.9 −9.4 6.5 40.9 13.3 12.1 −10.1 2.0 16.5 4.8 (1800) (−1060)  (730)(1370) (−1140)  (230) 46 14.0 −8.3 5.7 40.7 13.5 10.7 −8.8 1.9 17.8 5.4(1580) (−940) (640) (1210) (−990) (210)

Example 6 Samples 47-58

[0121] Polymer blends were made by melt blending various polymercompositions having different compositions and crystallinities withhydrocarbon resin EMPR 100 in the proportions indicated in Table 17, at175° C.-225° C. in a 250 cm³ Brabender internal mixer. The blends werethen fabricated into compression molded plaques and tested afterapproximately 7 days. Mechanical and hysteresis properties of the sevensamples were measured, and are reported in Tables 18 and 19,respectively. The “polymer type” indicated in Table 17 corresponds tothe designations of Table 1. TABLE 17 Composition Polymer Sample TypeAmount EMPR 100 # (Table 1) (wt %) (wt %) 47 D 88 12 48 D 84 16 49 D 8020 50 F 88 12 51 F 84 16 52 F 80 20 53 I 88 12 54 I 84 16 55 I 80 20 56J 88 12 57 J 84 16 58 J 80 20

[0122] TABLE 18 Mechanical and Thermal Properties Flex. Modulus 1%Tensile Sample secant M_(50%) M_(100%) M_(200%) M_(500%) ElongationStrength Tg # (psi (MPa) (psi (MPa)) (psi (MPa)) (psi (MPa)) (psi (MPa))(%) (psi (MPa)) (° C.) 47 417 65.9 80.5 80.1 57.7 133 83.1 −25.1 (2.88)(0.454)  (0.555)  (0.552)  (0.398)  (0.573) 48 390 61.0 74.3 74.9 54.2145.1 77.2 −23.2 (2.69) (0.421)  (0.512)  (0.516)  (0.374)  (0.532) 49365 58.8 70.9 71.7 53.5 142.5 73.4 −21.6 (2.52) (0.405)  (0.489) (0.494)  (0.369)  (0.506) 50 672 118 140.7 154.1 193.9 895 600 −23.2(4.63) (0.814)  (0.970) (1.06) (1.34) (4.14) 51 620 118 141 154 193 895600 −22.1 (4.27) (0.814)  (0.972) (1.06) (1.33) (4.14) 52 573 107 129142 167 935 507 −18.6 (3.95) (0.738)  (0.889)  (0.979) (1.15) (3.50) 531067 173 199 216 313 857 958 −22.4  (7.357) (1.19)  (1.37) (1.49) (2.16)(6.61) 54 941 170 203 224 319 851 992 −20.9 (6.49) (1.17)  (1.40) (1.54)(2.20) (6.84) 55 727 130 157 177 245 881 724 −19.3 (5.01) (0.896) (1.08)(1.22) (1.69) (4.99) 56 1275 205 239 257 411 820 1316 −21.5  (8.791)(1.41)  (1.65) (1.77) (2.83)  (9.074) 57 1080 180 214 236 363 835 1149−20.1  (7.447) (1.24)  (1.48) (1.63) (2.50)  (7.922) 58 943 157 188 211310 863 948 −19.3 (6.50) (1.08)  (1.30) (1.45) (2.14) (6.54)

[0123] TABLE 19 Hysteresis Properties Cycle 1 Cycle 2 Energy Energy LostEnergy Energy Lost Loading Unloading Energy Lost Tension LoadingUnloading Energy Lost Tension Sample (in. lb. (in. lb. (in. lb. EnergySet (in. lb. (in. lb. (in. lb. Energy Set # (mJ)) (mJ)) (mJ)) (%) (%)(mJ)) (mJ)) (mJ)) (%) (%) 47 4.5 −1.77 2.73 60.7 46.4 3.9 −2.0 1.9 48.762.4  (510) (−200) (308) (440) (−230) (210) 48 3.9 −1.44 2.46 63.1 48.03.9 −2.13 1.77 45.4 61.1  (440) (−163) (278) (440) (−241) (200) 49 3.7−1.48 2.22 60.0 44.1 3.63 −2.8 0.83 22.9 36.3  (420) (−167) (251) (410)(−320)  (94) 50 10.8 −6.8 4.0 37.0 17.8 9.16 −7.45 1.71 18.7 8 (1220)(−770) (450) (1040)  (−842) (196) 51 9.8 −6.1 3.7 37.8 19.2 8.5 −6.841.66 19.5 9.5 (1100) (−690) (420) (960) (−773) (188) 52 9.28 −5.82 3.4637.3 18.5 7.86 −6.23 1.63 20.7 9.88 (1050) (−658) (391) (888) (−704)(184) 53 14.5 −8.68 5.82 40.1 13.7 11.2 −9.26 1.94 17.3 5.0 (1640)(−981) (658) (1270)  (−1050)  (219) 54 14.62 −9.11 5.51 37.7 13.8 11.39−9.67 1.72 15.1 5.04 (1652) (−1030)  (623) (1287)  (−1090)  (194) 5510.74 −6.58 4.16 38.7 15.7 8.66 −7.05 1.61 18.6 7.38 (1214) (−744) (470)(979) (−797) (182) 56 17.03 −10.04 6.99 41.0 14.46 12.89 −10.57 2.3218.0 5.27 (1924) (−1135)  (790) (1457)  (−1194)  (262) 57 15.31 −9.286.03 39.4 14.22 11.83 −9.82 2.01 17.0 5.12 (1730) (−1050)  (681) (1337) (−1110)  (227) 58 13.32 −7.97 5.35 40.2 14.03 10.23 −8.35 1.88 18.4 5.72(1505) (−901) (605) (1156)  (−944) (212)

Example 7 Samples 59-70

[0124] Polymer blends were made by melt blending various polymercompositions having different compositions and crystallinities withhydrocarbon resin EMPR 104 in the proportions indicated in Table 20, at175° C.-225° C. in a 250 cm³ abender internal mixer. The blends werethen fabricated into compression molded plaques and tested afterapproximately 7 days. Mechanical and hysteresis properties of the sevensamples were measured, and are reported in Tables 21 and 22,respectively. The “polymer type” indicated in Table 20 corresponds tothe designations of Table 1. TABLE 20 Composition Polymer Sample TypeAmount EMPR 104 # (Table 1) (wt %) (wt %) 59 D 88 12 60 D 84 16 61 D 8020 62 F 88 12 63 F 84 16 64 F 80 20 65 I 88 12 66 I 84 16 67 I 80 20 68J 88 12 69 J 84 16 70 J 80 20

[0125] TABLE 21 Mechanical and Thermal Properties Flex. Modulus 1%Tensile Sample secant M_(50%) M_(100%) M_(200%) M_(500%) ElongationStrength Tg # (psi (MPa) (psi (MPa)) (psi (MPa)) (psi (MPa)) (psi (MPa))(%) (psi (MPa)) (° C.) 59 260 60 74 74 52 138 76 −26.6 (1.79) (0.41)(0.51) (0.51) (0.36) (0.52) 60 321 56 71 71 52 145 73 −24.3 (2.21)(0.39) (0.49) (0.49) (0.36) (0.50) 61 239 50 65 66 50 147 67 −23.6(1.65) (0.34) (0.45) (0.46) (0.34) (0.46) 62 839 137 167 185 253 868 848−23.9 (5.78)  (0.945) (1.15) (1.28) (1.74) (5.85) 63 636 106 133 149 183920 590 −22 (4.39)  (0.731)  (0.917) (1.03) (1.26) (4.07) 64 563 100 125140 169 922 515 −20.5 (3.88)  (0.690)  (0.862)  (0.965) (1.16) (3.55) 65987 159 191 212 323 848 1018 −23.2 (6.81) (1.10) (1.32) (1.46) (2.23) (7.019) 66 779 140 170 192 280 865 868 −21.6 (5.37)  (0.965) (1.17)(1.32) (1.93) (5.98) 67 736 119 147 173 245 857 675 −20.1 (5.07) (0.821) (1.01) (1.19) (1.69) (4.65) 68 1391 208 244 264 437 807 1423−22.4  (9.591) (1.43) (1.68) (1.82) (3.01)  (9.812) 69 1178 180 216 239376 828 1228 −21.2  (8.122) (1.24) (1.49) (1.65) (2.59)  (8.467) 70 972156 188 211 323 849 1020 −18.9 (6.70) (1.08) (1.30) (1.45) (2.23) (7.033)

[0126] TABLE 22 Hysteresis Properties Cycle 1 Cycle 2 Energy Energy LostEnergy Energy Lost Loading Unloading Energy Lost Tension LoadingUnloading Energy Lost Tension Sample (in. lb. (in. lb. (in. lb. EnergySet (in. lb. (in. lb. (in. lb. Energy Set # (mJ)) (mJ)) (mJ)) (%) (%)(mJ)) (mJ)) (mJ)) (%) (%) 59 4.04 −1.46 2.58 63.9 47.6 3.83 −1.91 1.9250.1 42  (457) (−165) (292) (433) (−216) (217) 60 3.86 −1.28 2.58 66.846.77 3.83 −1.91 1.92 50.1 41  (436) (−145) (292) (433) (−216) (217) 613.32 −1.11 2.21 66.6 49.06 3.68 −1.96 1.72 46.7 40.96  (375) (−125)(250) (416) (−221) (194) 62 11.74 −7.55 4.19 35.7 16.27 9.83 −8.29 1.5415.7 6.21 (1327) −(−853)  (473) (1110)  (−937) (174) 63 9.33 −5.88 3.4537.0 19.44 8.06 −6.45 1.61 20.0 9.06 (1050) (−664) (390) (911) (−729)(182) 64 8.62 −5.33 3.29 38.2 20.13 7.47 −5.86 1.61 21.6 10.19  (974)(−602) (372) (844) (−662) (182) 65 13.21 −8.10 5.11 38.7 14.85 10.51−8.78 1.73 16.5 5.74 (1493) (−915) (577) (1188)  (−992) (195) 66 11.95−7.37 4.58 38.3 15.65 9.63 −7.96 1.67 17.3 6.241 (1350) (−833) (518)(1090)  (−899) (189) 67 10.60 −6.34 4.26 40.2 16.20 8.54 −6.92 1.62 19.07.37 (1198) (−716) (481) (965) (−782) (183) 68 16.91 −9.77 7.14 42.215.36 12.9 −10.6 2.30 17.8 5.96 (1911) (−1100)  (807)  (1460)1  (−1199)1(260) 69 14.97 −8.93 6.04 40.3 14.83 11.46 −9.52 1.94 16.9 5.67 (1692)(−1010)  (683) (1295)  (−1076)  (219) 70 12.99 −7.80 5.19 40.0 14.8710.19 −8.43 1.76 17.3 6.18 (1468) (−881) (586) (1151)  (−953) (199)

Example 8 Samples 71-82

[0127] Polymer blends were made by melt blending polymer-H with variousresins in the proportions indicated in Table 23, at 175° C.-225° C. in a250 cm³ Brabender internal mixer. The blends were then fabricated intocompression molded plaques and tested after approximately 7 days.Mechanical and hysteresis properties of the seven samples were measured,and are reported in Tables 24 and 25, respectively. In Table 23, TOPASis a high Tg polymer made with alternating norbornene and ethylene. InTable 24, MFR is the ASTM 1238 Procedure A (230° C., 2.16 kg), Tg andΔH_(fus), are first melt values, and Flex Modules is the 1% secantvalue. TABLE 2 3 Composition Sample polymer-H Polystyrene TOPAS EMPR 104EMPR 100 # (wt %) (wt %) (wt %) (wt %) (wt % 71 80 0 0 20 0 72 80 4 0 160 73 80 8 0 12 0 74 80 12 0 8 0 75 80 16 0 4 0 76 80 20 0 0 0 77 80 0 00 20 78 80 0 4 0 16 79 80 0 8 0 12 80 80 0 12 0 8 81 80 0 16 0 4 82 80 020 0 0

[0128] TABLE 24 Mechanical and Thermal Properties MFR Tg of ΔH_(fus)ofFlex. Tensile Sample (g/10 polymer-H polymer-H Modulus M_(50%) M_(100%)M_(200%) M_(500%) Elasticity Strength # min.) (° C.) (J/g) (psi (MPa)(psi (MPa)) (psi (MPa)) (psi (MPa)) (psi (MPa)) (%) (psi (MPa)) 71 4.76−20.2 2.6 655 91.5 111 119 123 984 319 (4.52) (0.631)  (0.765)  (0.821) (0.848) (2.20) 72 4.59 −22.2 2.7 764 108 130 140 168 940 482 (5.27)(0.745)  (0.896)  (0.965) (1.16) (3.32) 73 4.45 −22.9 2.8 814 116 139147 208 944 593 (5.61) (0.800)  (0.958) (1.01) (1.43) (4.09) 74 4.33−25.2 3.1 910 131 151 158 255 909 605 (6.27) (0.903) (1.04) (1.09)(1.76) (4.17) 75 3.98 −27.2 3.6 1212 146 167 177 297 943 711  (8.357)(1.01)  (1.15) (1.22) (2.05) (4.90) 76 3.92 −29 4.7 1485 163 185 201 309985 772 (10.24) (1.12)  (1.28) (1.39) (2.13) (5.32) 77 4.84 * * 700 79.194.9 99.4 89.7 * 213 (4.83) (0.545)  (0.654)  (0.685)  (0.618) (1.47) 784.44 * * 826 100 118 122 130 972 459 (5.69) (0.690)  (0.814)  (0.841) (0.896) (3.16) 79 4.25 * * 965 138 157 160 293 835 1007 (6.65) (0.952)(1.08) (1.10) (2.02)  (6.943) 80 4.22 * * 974 151 169 175 418 855 1251(6.72) (1.04)  (1.16) (1.21) (2.88)  (8.626) 81 3.87 * * 1168 167 185198 560 798 1246  (8.053) (1.15)  (1.28) (1.36) (3.86)  (8.591) 823.73 * * 1450 204 222 255 867 694 1240  (9.998) (1.41)  (1.53) (1.76)(5.98)  (8.550)

[0129] TABLE 25 Hysteresis Properties Cycle 1 Cycle 2 Energy Energy LostEnergy Energy Lost Loading Unloading Energy Lost Tension LoadingUnloading Energy Lost Tension Sample (in. lb. (in. lb. (in. lb. EnergySet (in. lb. (in. lb. (in. lb. Energy Set # (mJ)) (mJ)) (mJ)) (%) (%)(mJ)) (mJ)) (mJ)) (%) (%) 71 7.5 −4.3 3.2 42.67 24.1 6.3 −4.6 1.7 26.9816.6  (850) (−490) (360) (710) (−520) (190) 72 8.8 −4.8 4.0 45.45 23.97.3 −5.2 2.1 28.77 16.4  (990) (−540) (450) (820) (−590) (240) 73 8.8−4.1 4.7 53.41 28.0 7.8 −5.3 2.5 32.05 20.7  (990) (−460) (530) (880)(−600) (280) 74 8.6 −3.4 5.2 60.47 33.1 8.0 −5.1 2.9 36.25 25.7  (970)(−380) (590) (900) (−580) (330) 75 10.2 −4.3 5.9 57.84 28.3 8.6 −5.2 3.439.53 28.3 (1150) (−490) (670) (970) (−590) (380) 76 13.1 −5.8 7.3 55.7335.0 10.5 −6.3 4.2 40 27.3 (1480) (−650) (820) (1190)  (−710) (470) 775.7 −2.78 2.92 51.2 29.77 5.4 −3.69 1.71 31.7 21.87  (640) (−314) (330)(610) (−417) (193) 78 7.0 −2.88 4.14 59.0 21.49 7.0 −4.64 2.36 33.721.49  (790) (−325) (468) (790) (−524) (267) 79 8.9 −3.49 5.4 60.7 24.938.89 −5.09 3.8 42.7 15.95 (1000) (−394) (610) (1000)  (−575) (430) 809.7 −3.81 13.53 139.2 25.33 9.26 −6.4 2.86 30.9 16.67 (1100) (−431)(1529)  (1050)  (−720) (323) 81 15.6 −8.23 7.35 47.2 21.3 11.84 −8.343.5 29.6 13.41 (1760) (−930) (831) (1338)  (−942) (400) 82 17.2 −8.858.39 48.7 20.64 12.89 −9.07 3.82 29.6 13.13 (1940) (−1000)  (948)(1457)  (−1020)  (432)

[0130] Various tradenames used herein are indicated by a ™ symbol,indicating that the names may be protected by certain trademark rights.Some such names may also be registered trademarks in variousjurisdictions.

[0131] All patents, test procedures, and other documents cited herein,including priority documents, are fully incorporated by reference to theextent such disclosure is not inconsistent with this invention and forall jurisdictions in which such incorporation is permitted.

[0132] While the illustrative embodiments of the invention have beendescribed with particularity, it will be understood that various othermodifications will be apparent to and can be readily made by thoseskilled in the art without departing from the spirit and scope of theinvention. Accordingly, it is not intended that the scope of the claimsappended hereto be limited to the examples and descriptions set forthherein but rather that the claims be construed as encompassing all thefeatures of patentable novelty which reside in the present invention,including all features which would be treated as equivalents thereof bythose skilled in the art to which the invention pertains.

[0133] When numerical lower limits and numerical upper limits are listedherein, ranges from any lower limit to any upper limit are contemplated.

What is claimed is:
 1. A composition comprising: (a) from 70% to 95% byweight based on the total weight of the composition of a polymerselected from the group consisting of homopolymers and random copolymersof propylene, the polymer having a heat of fusion as determined by DSCof less than 50 J/g and a melt index (MI) of less than 20 dg/min, andcontaining stereoregular propylene crystallinity; and (b) from 5% to 30%by weight based on the total weight of the composition of a misciblehydrocarbon resin having a glass transition temperature greater than 20°C.
 2. The composition of claim 1, wherein the composition has a tensionset of less than 20%.
 3. The composition of claim 1, wherein thecomposition has a tension set of less than 12%.
 4. The composition ofclaim 1, wherein the composition has a tension set of less than 10%. 5.The composition of claim 1, wherein the composition has a tension set TSand a 500% modulus M_(500%) conforming to the relationship: TS<≦01*M_(500%)+12.5, where M is in units of psi.
 6. The composition of claim 1,wherein the composition has a single glass transition temperature atleast 1° C. lower than the glass transition temperature of thehydrocarbon resin.
 7. The composition of claim 1, wherein thecomposition has a tensile modulus at least 10% lower than the tensilemodulus of the polymer.
 8. The composition of claim 1, wherein thepolymer has isotactic stereoregular propylene crystallinity.
 9. Thecomposition of claim 1, wherein the polymer is a random copolymer ofpropylene and at least one comonomer selected from ethylene, C₄-C₁₂α-olefins, and combinations thereof.
 10. The composition of claim 9,wherein the polymer has a narrow compositional distribution, and amelting point as determined by DSC of from 25° C. to 110° C.
 11. Thecomposition of claim 9, wherein the comonomer comprises ethylene. 12.The composition of claim 11, wherein the polymer comprises from 2 wt %to 25 wt % polymerized ethylene units, based on the total weight of thepolymer.
 13. The composition of claim 1, wherein the polymer has a heatof fusion as determined by DSC of from 1 J/g to 50 J/g.
 14. Thecomposition of claim 1, wherein the polymer has a heat of fusion asdetermined by DSC of from 3 J/g to 10 J/g.
 15. The composition of claim1, wherein the polymer has a melting point as determined by DSC of from35° C. to 70° C.
 16. The composition of claim 1, wherein the polymer hasa molecular weight distribution Mw/Mn of from 2.0 to 4.5.
 17. Thecomposition of claim 1, wherein the polymer has a melt index (MI) ofless than 2 dg/min.
 18. The composition of claim 1, wherein the polymeris present in the composition in an amount of from 80 to 95 wt % and thehydrocarbon resin is present in an amount of from 5 to 20 wt %, based onthe total weight of the composition.
 19. The composition of claim 1,wherein the hydrocarbon resin is a hydrogenated cycloaliphatic resin.20. The composition of claim 1, wherein the hydrocarbon resin has amolecular weight (Mn) of from 200 to
 5000. 21. The composition of claim1, wherein the hydrocarbon resin has a molecular weight (Mn) of from 200to
 1000. 22. The composition of claim 1, wherein the hydrocarbon resinhas a molecular weight (Mn) of from 500 to
 1000. 23. The composition ofclaim 1, wherein the hydrocarbon resin has a softening point of from 80°C. to 180° C.
 24. The composition of claim 1, wherein the hydrocarbonresin has a softening point of from 120° C. to 150° C.
 25. Thecomposition of claim 1, wherein the hydrocarbon resin has a softeningpoint of from 125° C. to 140° C.
 26. A composition comprising: (a) apolymer selected from the group consisting of homopolymers and randomcopolymers of propylene, wherein the polymer has a heat of fusion asdetermined by DSC of less than 50 J/g, a melt index (MI) of less than 5dg/min, and contains stereoregular propylene crystallinity; and (b) amiscible hydrocarbon resin having a glass transition temperature greaterthan 20° C.
 27. The composition of claim 26, wherein the polymer ispresent in the composition in an amount of from 80 to 99 wt % and thehydrocarbon resin is present in an amount of from 1 to 20 wt %, based onthe total weight of the composition.
 28. The composition of claim 26,wherein the polymer is present in the composition in an amount of from80 to 95 wt % and the hydrocarbon resin is present in an amount of from5 to 20 wt %, based on the total weight of the composition.
 29. Thecomposition of claim 26, wherein the composition has a tension set ofless than 20%.
 30. The composition of claim 26, wherein the compositionhas a tension set of less than 12%.
 31. The composition of claim 26,wherein the composition has a tension set of less than 10%.
 32. Thecomposition of claim 26, wherein the composition has a tension set TSand a 500% modulus M_(500%) conforming to the relationship: TS≦0.01*M_(500%)+12.5, where M is in units of psi.
 33. The composition of claim26, wherein the composition has a single glass transition temperature atleast 1° C. lower than the glass transition temperature of thehydrocarbon resin.
 34. The composition of claim 26, wherein thecomposition has a tensile modulus at least 10% lower than the tensilemodulus of the polymer.
 35. The composition of claim 26, wherein thepolymer has isotactic stereoregular propylene crystallinity.
 36. Thecomposition of claim 26, wherein the polymer is a random copolymer ofpropylene and at least one comonomer selected from the group consistingof ethylene, C₄-C₁₂ α-olefins, and combinations thereof.
 37. Thecomposition of claim 36, wherein the polymer has a narrow compositionaldistribution, and a melting point as determined by DSC of from 25° C. to110° C.
 38. The composition of claim 36, wherein the comonomer comprisesethylene.
 39. The composition of claim 38, wherein the polymer comprisesfrom 2 wt % to 25 wt % polymerized ethylene units, based on the totalweight of the polymer.
 40. The composition of claim 26, wherein thepolymer has a heat of fusion as determined by DSC of from 1 J/g to 50J/g.
 41. The composition of claim 26, wherein the polymer has a heat offusion as determined by DSC of from 3 J/g to 10 J/g.
 42. The compositionof claim 26, wherein the polymer has a melting point as determined byDSC of from 35° C. to 70° C.
 43. The composition of claim 26, whereinthe polymer has a molecular weight distribution Mw/Mn of from 2.0 to4.5.
 44. The composition of claim 26, wherein the polymer has a meltindex (MI) of less than 2 dg/min.
 45. The composition of claim 26,wherein the hydrocarbon resin is a hydrogenated cycloaliphatic resin.46. The composition of claim 26, wherein the hydrocarbon resin has amolecular weight (Mn) of from 200 to
 5000. 47. The composition of claim26, wherein the hydrocarbon resin has a molecular weight (Mn) of from200 to
 1000. 48. The composition of claim 26, wherein the hydrocarbonresin has a molecular weight (Mn) of from 500 to
 1000. 49. Thecomposition of claim 26, wherein the hydrocarbon resin has a softeningpoint of from 80° C. to 180° C.
 50. The composition of claim 26, whereinthe hydrocarbon resin has a softening point of from 120° C. to 150° C.51. The composition of claim 26, wherein the hydrocarbon resin has asoftening point of from 125° C. to 140° C.
 52. An elastic filmcomprising a composition, the composition comprising: (a) a polymerselected from the group consisting of homopolymers and random copolymersof propylene, wherein the polymer has a heat of fusion as determined byDSC of from 1 J/g to 50 J/g, a melt index (MI) of less than 7 dg/min,and contains stereoregular propylene crystallinity; and (b) a misciblehydrocarbon resin with a glass transition temperature greater than 20°C.
 53. The film of claim 52, wherein the film is a monolayer film. 54.The film of claim 52, wherein the film is a multilayer film.
 55. Agarment structure comprising the film of claim
 53. 56. The garmentstructure of claim 55, wherein the garment structure is a diaper or anincontinence garment.